Single-layer lithium ion battery separators exhibiting high low shrinkage rates at high temperatures

ABSTRACT

An insulating (nonconductive) microporous polymeric battery separator comprised of a single layer of enmeshed microfibers and nanofibers is provided. Such a separator accords the ability to attune the porosity and pore size to any desired level through a single nonwoven fabric. Through a proper selection of materials as well as production processes, the resultant battery separator exhibits isotropic strengths, low shrinkage, high wettability levels, and pore sizes related directly to layer thickness. The overall production method is highly efficient and yields a combination of polymeric nanofibers within a polymeric microfiber matrix and/or onto such a substrate through high shear processing that is cost effective as well. The separator, a battery including such a separator, the method of manufacturing such a separator, and the method of utilizing such a separator within a battery device, are all encompassed within this invention.

FIELD OF THE INVENTION

The present invention relates to an insulating (nonconductive) microporous polymeric battery separator comprised of a single layer of enmeshed microfibers and nanofibers. Such a separator accords the ability to attune the porosity and pore size to any desired level through a single nonwoven fabric. Through a proper selection of materials as well as production processes, the resultant battery separator exhibits isotropic strengths, low shrinkage, high wettability levels, and pore sizes related directly to layer thickness. The overall production method is highly efficient and yields a combination of polymeric nanofibers within a polymeric microfiber matrix and/or onto such a substrate through high shear processing that is cost effective as well. The separator, a battery including such a separator, the method of manufacturing such a separator, and the method of utilizing such a separator within a battery device, are all encompassed within this invention.

BACKGROUND OF THE INVENTION

Batteries have been utilized for many years as electrical power generators in remote locations. Through the controlled movement of ions between electrodes (anode and cathode), a power circuit is generated, thereby providing a source of electricity that can be utilized until the excess ions in one electrode are depleted and no further electrical generation is possible. In more recent years, rechargeable batteries have been created to allow for longer lifetimes for such remote power sources, albeit through the need for connecting such batteries to other electrical sources for a certain period of time. All in all, however, the capability of reusing such a battery has led to greater potentials for use, particularly through cell phone and laptop computer usage and, even more so, to the possibility of automobiles that solely require electricity to function.

Such batteries typically include at least five distinct components. A case (or container) houses everything in a secure and reliable manner to prevent leakage to the outside as well as environmental exposure inside. Within the case are an anode and a cathode, separated effectively by a separator, as well as an electrolyte solution (low viscosity liquid) that transport ions through the separator between the anode and cathode. The rechargeable batteries of today and, presumably tomorrow, will run the gamut of rather small and portable devices, but with a great deal of electrical generation potential in order to remain effective for long periods between charging episodes, to very large types present within automobiles, as an example, that include large electrodes (at least in surface area) that must not contact one another and a large number of ions that must consistently and constantly pass through a membrane to complete the necessary circuit, all at a level of power generation conducive to providing sufficient electricity to run an automobile motor. As such, the capability and versatility of battery separators in the future must meet certain requirements that have yet to be provided within the current industry.

Generally speaking, battery separators have been utilized since the advent of closed-cell batteries to provide necessary protection from unwanted contact between electrodes as well as to permit effective transport of electrolytes within power generating cells. Typically, such materials have been of film structure, sufficiently thin to reduce the weight and volume of a battery device while imparting the necessary properties noted above at the same time. Such separators must exhibit other characteristics, as well, to allow for proper battery function. These include chemical stability, suitable porosity of ionic species, effective pore size for electrolyte transfer, proper permeability, effective mechanical strength, and the capability of retaining dimensional and functional stability when exposed to high temperatures (as well as the potential for shutdown if the temperature rises to an abnormally high level).

In greater detail, then, the separator material must be of sufficient strength and constitution to withstand a number of different scenarios. Initially, the separator must not suffer tears or punctures during the stresses of battery assembly. In this manner, the overall mechanical strength of the separator is extremely important, particularly as high tensile strength material in both the machine and cross (i.e., transverse) directions allows the manufacturer to handle such a separator more easily and without stringent guidelines lest the separator suffer structural failure or loss during such a critical procedure. Additionally, from a chemical perspective, the separator must withstand the oxidative and reductive environment within the battery itself, particularly when fully charged. Any failure during use, specifically in terms of structural integrity permitting abnormally high amounts of current to pass or for the electrodes to touch, would destroy the power generation capability and render the battery totally ineffective. Thus, even above the ability to weather chemical exposure, such a separator must also not lose dimensional stability (i.e., warp or melt) or mechanical strength during storage, manufacture, and use, either, for the same reasons noted above.

Simultaneously, however, the separator must be of proper thickness to, in essence, facilitate the high energy and power densities of the battery, itself. A uniform thickness is quite important, too, in order to allow for a long life cycle as any uneven wear on the separator will be the weak link in terms of proper electrolyte passage, as well as electrode contact prevention.

Additionally, such a separator must exhibit proper porosity and pore sizes to accord, again, the proper transport of ions through such a membrane (as well as proper capacity to retain a certain amount of liquid electrolyte to facilitate such ion transfer during use). The pores themselves should be sufficiently small to prevent electrode components from entering and/or passing through the membrane, while also allowing, again, as noted above, for the proper rate of transfer of electrolyte ions. As well, uniformity in pore sizes, as well as pore size distribution, provides a more uniform result in power generation over time as well as more reliable long-term stability for the overall battery as, as discussed previously, uniform wear on the battery separator, at least as best controlled in such a system, allows for longer life-cycles. It additionally can be advantageous to ensure the pores therein may properly close upon exposure to abnormally high temperatures to prevent excessive and undesirable ion transfer upon such a battery failure (i.e., to prevent fires and other like hazards).

As well, the pore sizes and distributions may increase or decrease the air resistance of the separator, thus allowing for simple measurements of the separator that indicate the ability of the separator to allow adequate passage of the electrolyte present within the battery itself. For instance, mean flow pore size can be measured according to ASTM E-1294, and this measurement can be used to help determine the barrier properties of the separator. Thus, with low pore size, the rigidity of the pores themselves (i.e., the ability of the pores to remain a certain size during use over time and upon exposure to a set pressure) allows for effective control of electrode separation as well. More importantly, perhaps, is the capability of such pore size levels to limit dendrite formation in order to reduce the chances of crystal formation on an anode (such a lithium crystals on a graphite anode) that would deleteriously impact the power generation capability of the battery over time.

Furthermore, the separator must not impair the ability of the electrolyte to completely fill the entire cell during manufacture, storage and use. Thus, the separator must exhibit proper wicking and/or wettability during such phases in order to ensure the electrolyte in fact may properly transfer ions through the membrane; if the separator were not conducive to such a situation, then the electrolyte would not properly reside on and in the separator pores and the necessary ion transmission would not readily occur. Additionally, it is understood that such proper wettability of the separator is generally required in order to ensure liquid electrolyte dispersion on the separator surface and within the cell itself. Non-uniformity of electrolyte dispersion may result in dendritic formations within the cell and on the separator surface, thereby creating an elevated potential for battery failures and short circuiting therein.

There is also great concern with the dimensional stability of such a separator when utilized within a typical lithium ion cell, as alluded to above. The separator necessarily provides a porous barrier for ion diffusion over the life of the battery, certainly. However, in certain situations, elevated temperatures, either from external sources or within the cell itself, may expose susceptible separator materials to undesirable shrinking, warping, or melting, any of which may deleteriously affect the capability of the battery over time. As such, since reduction of temperature levels and/or removal of such battery types from elevated temperatures during actual utilization are very difficult to achieve, the separator itself should include materials that can withstand such high temperatures without exhibiting any appreciable effects upon exposure. Alternatively, the utilization of combinations of materials wherein one type of fiber, for instance, may provide such a beneficial result while still permitting the separator to perform at its optimum level, would be highly attractive.

To date, however, as noted above, the standards in place today do not comport to such critical considerations. The general aim of an effective battery separator is to provide such beneficial characteristics all within a single thin sheet of material. The capability to provide low air resistance, very low pore size and suitable pore size distribution, dimensional stability under chemical and elevated temperature environments, proper wettability, optimal thickness to permit maximum battery component presence in the smallest enclosure possible, and effective overall tensile strength (and preferably isotropic in nature), are all necessary in order to accord a material that drastically reduces any potential for electrode contact, but with the capability of controlled electrolyte transport from one portion of the battery cell to the other (i.e., closing the circuit to generate the needed electrical power), in other words for maximum battery output over the longest period of time with the least amount of cell volume. Currently, such properties are not effectively provided in tandem to such a degree. For instance, Celgard has disclosed and marketed an expanded film battery separator with very low pore size, which is very good in that respect, as noted above; however, the corresponding air resistance for such a material is extremely high, thus limiting the overall effectiveness of such a separator. To the contrary, duPont commercializes a nanofiber nonwoven membrane separator that provides very low air resistance, but with overly large pore sizes therein. Additionally, the overall mechanical strengths exhibiting by these two materials are very limiting; the Celgard separator has excellent strength in the machine direction, but nearly zero strength in the cross (transverse) direction. Such low cross direction strength requires very delicate handling during manufacture, at least, as alluded to above. The duPont materials fare a little better, except that the strengths are rather low in both directions, albeit with a cross direction that is higher than the Celgard material. In actuality, the duPont product is closer to an isotropic material (nearly the same strengths in both machine and cross directions), thus providing a more reliable material in terms of handling than the Celgard type. However, the measured tensile strengths of the duPont separator are quite low in effect, thus relegating the user to carefully maneuvering and placing such materials during manufacture as well. Likewise, the dimensional stability of such prior battery separators are highly suspect due to these tensile strength issues, potentially leading to materials that undesirably lose their structural integrity over time when present within a rechargeable battery cell.

Thus, there still exists a need to provide a battery separator that simultaneously provides all of these characteristics for long-term, reliable, lithium battery results. As such, although such a separator exhibiting low air resistance and low pore size, as well as high tensile strength overall and at relatively isotropic levels, proper chemical stability, structural integrity, and dimensional stability (particularly upon exposure to elevated temperatures), although highly desired, to date there has been a decided lack of provision of such a prized separator material. Additionally, a manner of producing battery separators that allows for achieving such desired targeted property levels through efficient manufacturing processes would also be highly desired, particularly if minor modifications in materials selection, etc., garners such beneficial results and requirements on demand; currently, such a manufacturing method to such an extent has yet to be explored throughout the battery separator industry. As such, an effective and rather simple and straightforward battery separator manufacturing method in terms of providing any number of membranes exhibiting such versatile end results (i.e., targeted porosity and air resistance levels through processing modifications on demand) as well as necessary levels of mechanical properties, heat resistance, permeability, dimensional stability, shutdown properties, and meltdown properties, is prized within the rechargeable battery separator industry; to date, such a material has been unavailable.

ADVANTAGES AND SUMMARY OF THE INVENTION

A distinct advantage of the present invention is the ease in manufacturing through a wet-laid nonwoven fabrication process. Another distinct advantage is the resulting capability of providing any targeted level of pore size, porosity, and air resistance, through the mere change in proportions of component fibers utilized during the fabrication process, as well as the proper calendering of the produced single layer material. Yet another advantage of this inventive battery separator is the isotropic strength properties accorded the user for reliability in long-term use as well as during the battery manufacturing phase. The ability of the inventive separator to provide contemporaneous low air resistance and low pore sizes is still a further advantage of this invention. Yet another advantage of this inventive battery separator is the provision of a specifically non-conductive (and thus insulating) fabric (or paper) that does not allow transmission of electrical charge through the separator body, but solely through the transport of charged ions through the pores present within its structure. Yet another advantage is the high porosity of the material, allowing more ions to flow and increasing the durability of the ability to hold energy over many life cycles by allowing fully recharged electrodes. Other advantages include, without limitation, the ability to dial in certain physical characteristics through the proper selection of fibrous materials prior to layer formation, as well as the utilization of all micro fibers initially and the generation of nanofibers (in fibrillated form) through high shear treatment thereof and thus the capability of forming all the necessary separator components from a single starting material. Of particular advantage is the capability of such separators to withstand high temperature exposure in use and low shrinkage rates, with no appreciable loss in performance.

Accordingly, this invention pertains to a polymeric battery separator comprising a nonwoven combination of microfibers and nanofibers, wherein said single layer of said separator exhibits an isotropic tensile strength wherein the machine direction tensile strength is less than three times the cross direction tensile strength. Said separator also exhibits a machine direction (MD) tensile strength greater than 90 kg/cm² and less than 1,000 kg/cm², a cross direction (CD) tensile strength greater than 30 kg/cm² and less than 1,000 kg/cm², and a mean flow pore size less than 0.80 μm. Furthermore, such an invention includes a battery separator as defined and comprising a single layer of fibers, said layer comprising both nanofibers and microfibers, said nanofibers having an average maximum width less than 1000 nm, said microfibers having a maximum width greater than 3000 nanometers, and said nanofibers and microfibers intermingled such that at least a portion of said nanofibers reside in the interstices between said microfibers. Additionally, the invention encompasses a method of forming a battery separator, wherein said battery separator exhibits a maximum thickness of 250 microns, and wherein said battery separator includes a combination of microfiber and nanofiber constituents, said method comprising the steps of a) providing an aqueous solvent; b) introducing therein a plurality of nanofibers and a plurality of microfibers to form a microfiber/nanofiber dispersion within an aqueous solvent; c) mixing said microfiber/nanofiber dispersion under high shear conditions; d) introducing said highly sheared dispersion within a paper making machine; e) producing a web of microfiber/nanofiber material; and f) drying said web. The method including a further process step of treating such a web by with a calendering procedure to produce a separator material exhibiting a thickness of at most 100 microns and a pore size of at most 2000 nm, is also contemplated.

Additionally, this invention encompasses an insulating, nonconductive microporous polymeric battery separator comprised of a single layer of enmeshed microfibers and nanofibers, wherein said battery separator further shrinks less than 5% when exposed to a temperature of 200° C. for 1 hour. Such a separator may also comprise fibers of length less than 2.54 cm (1 inch), such fibers comprising at least 5% of thermally stable fibers that have no melting point, glass transition temperature or thermal degradation below about 300° C., such battery separator having a mean flow pore size less than 2000 nm. As well, such a battery separator of claim 1 exhibiting a mean flow pore size of less than 2000 nm, preferably less than 1000 nm, is encompassed, too. Other properties of the inventive separator include the presence of fibrillated microfibers, microfibers exhibiting an average fiber diameter greater than 1000 nm (preferably greater than 3000 nm), nanofibers exhibiting an average fiber diameter less than 1000 nm (preferably less than than 700 nm), and nanofibers exhibiting a a transverse aspect ratio greater than 1.5:1.

Throughout this disclosure, the term microfiber is intended to mean any polymeric fiber exhibiting a width that is measured in micrometers, generally having a maximum width greater than 1000 nm, but also greater than 3000 nm, or even greater than 5000 nm or possibly even greater than 10,000 nm, up to about 40 microns. As well, the term nanofiber is intended to mean any polymeric fiber exhibiting a width that is measured in nanometers, generally having a maximum width less than 1000 nm, but possibly less than 700 nm, or even less than 500 nm or possibly even less than 300 nm (as low as about 1 nm). For either micro fiber or nanofiber materials, it should be understood that width may be considered diameter, although in such a situation, diameter would be considered a mean diameter since uniformity of fiber structure is typically very difficult to achieve. Thus, maximum width is utilized as the primary definition, particularly if the fibers themselves are not cylindrical in shape, thus allowing for the possibility of square, rectangle, triangle, or other geometric shape(s) for such fibers, which would all be within the scope of breadth of this invention as long as the proper micro- and nano-fiber measurements are present. As well, the term insulating in intended to indicate no appreciable degree of electrical conductivity, and thus the inventive fabric structure does not permit electrical charge throughout the fabric body, but only through the passage of electrolytic ions through the pores present therein.

Such a combination of microfibers and nanofibers has yet to be investigated within the battery separator art, particularly in terms of the capability of providing a single-layer nonwoven fabric of the two base components for such a purpose. The combination is particularly important, as it provides a nonwoven with a bimodal distribution of fiber diameters and lengths, such that the average length of the microfibers is at least 5 times the average length of the nanofibers, preferably longer than 10 times the average length of the nanofibers, and most preferably longer than 20 times the length of the nanofibers. Additionally, the diameters are also in a bimodal distribution, such that the average diameter of the microfibers is more than 3 times the average diameter of the nanofibers, preferably more than 5 times the average diameter of the nanofibers, and most preferably more than 10 times the average diameter of the nanofibers. This bimodal distribution allows the microfibers to provide strength, loft, permeability, modulus, tear and puncture resistance, wet strength, processability, and other features that the nanofibers could not provide on their own.

The microfiber constituent may be of any suitable polymer that provides the necessary chemical and heat resistance alluded to above, as well as the capability of forming a microfiber structure. As well, such a microfiber may also be fibrillated (or treated in any other like manner, such as through plasma exposure, and the like) during or subsequent to fiber formation in order to increase the surface area thereof to facilitate the desired entangling between a plurality of such microfibers during a nonwoven fabrication process. Such polymeric components may thus include acrylics such as polyacrylonitrile, polyolefins such as polypropylene, polyethylene, polybutylene and others including copolymers, polyamides, polyvinyl alcohol, polyethylene terephthalate, polybutylene terephthalate, polysulfone, polyvinyl fluoride, polyvinylidene fluoride, polyvinylidene fluoride-hexafluoropropylene, polymethyl pentene, polyphenylene sulfide, polyacetyl, polyurethane, aromatic polyamide, semi-aromatic polyamide, polypropylene terephthalate, polymethyl methacrylate, polystyrene, cellulosic polymers (rayon, as one non-limiting example), polyaramids, including para-aramids and meta-aramids, and blends, mixtures and copolymers including these polymers. Polyacrylates, cellulosic polymers, and polyaramids are potentially preferred. Such materials provide a range of highly desirable properties that function in combination with the properties of the other polymer types to accord overarching beneficial results in terms of tensile strength, high temperature protection, wettability, and pore size capability, particularly when included as nanofiber components with like microfiber bases. Such microfibers may also be pre-treated with adhesives to effectuate the desired degree of contact and dimensional stability of the overall nonwoven structure subsequent to fabrication.

Additionally, the microfibers may be selected in terms of individual fiber properties to provide combinations of materials that accord desirable characteristics to the overall battery separator. Thus, since poly-aramid, meta-aramid, and cellulosic fibers provide excellent heat resistance and certain strength benefits, such fibers may be incorporated individually (as wet-laid constituents, for example) or in combination through entanglement or other means. Such fibers must be of sufficient length to impart the necessary strength to the overall separator but short enough to permit proper incorporation (such as, again, for instance, within a wet-laid procedure). For instance, they may preferably be longer than 0.5 mm, more preferably longer than 1 mm, and most preferably longer than 2 mm.

Microfibers or nanofibers may preferentially be of a material that will melt or flow under pressure or high temperature. It is of particular benefit to have one constituent which will melt or flow at a temperature that is lower than the other constituents. For example, polyester microfibers can be made to flow at temperatures approaching the melt temperature of 260° C. Additionally, polyacrylonitrile microfibers or nanofibers can be made to flow under high pressure and temperature. Cellulose, rayon, aramid, and other micro- or nanofibers will not flow under these temperatures. Thus, a combination of materials comprising at least one fiber that will flow under high temperature and/or pressure and at least one fiber that will not flow under the same temperature and/or pressure will enable the first fiber to bond the other fibers together, imparting additional strength to the nonwoven separator.

The nanofibers may thus be of any like polymer constituency and/or combination in order to withstand the same types of chemical and high temperature exposures as for the microfibers. Due to their size, there is no requirement of post-manufacture treatment of such nanofiber materials to accord any increase in entanglement on the produced nonwoven surface or within the interstices thereof. Nanofiber generation, however, may be provided through a high shear treatment of microfiber sources in order to strip nanosized constituents there from as materials that meet the definition of nanofiber, above. In this manner, too, such peeled or stripped nanofibers will exhibit a fibrillated appearance and performance such that improvements in entanglement within the interstices of the microfibers during separator production may occur (not to mention the potential for improved entanglement between individual nanofibers prior to and/or during the same separator manufacturing procedure). In such a situation, the microfiber and nanofiber materials may thus be from the same material, with portions of the microfiber material removed to form the nanofiber constituents, and such nanofibers may have varying and multiple lengths as well as varied cross sections and overall sizes. In any event, nanofiber production may be undertaken in this manner with the removed constituents from the microfiber source collected and utilized in such forms with other types of microfibers, not just those from which such nanofibers have been provided. In such embodiments of the inventive battery separator, any type of nanofiber may be utilized for such a purpose. Preferably, however, the capability of providing nanofibers that exhibit potentially beneficial properties, such as high temperature stability, tensile strength, and the like, may create a situation wherein specific fiber types are utilized.

Although such “fibrillated” nanofibers may be utilized are described, specifically produced nanofiber components may be incorporated with such microfiber base materials to permit the inventive result of a separator sheet with certain pore sizes produced through a wet-laid process. Such a manufacturing process thus includes the introduction of nanofiber components within a microfiber solution in a dilute wet state, mixing the same under high shear conditions, and then drying to form a resultant sheet. This sheet may then be calendered in order to reduce the sheet thickness as desired, but, in addition, to further dial in the optimal pore sizes and pore size distribution present therein. With a resilient sheet of properly dispersed and incorporated microfiber and nanofiber components, this wet-laid process permits suitable sheet production wherein the amount of nanofiber dictates the capacity to fill the interstices between microfiber constituents, thus creating the desired pores within the resultant sheet. The calendering operation may then permit a correlative value of sheet thickness to pore size, particularly due to the overall tensile strength of the sheet subsequent to wet-laid production. Such a process thus provides a relatively simple, yet elegant method to provide the capability of optimizing pore size distribution and size without having to extrude or otherwise manipulate the overall structure in a manner that may deleteriously tear, warp, and/or obfuscate the dimensional stability thereof. Additionally, the ability to utilize a simple microfiber/nanofiber/water solution for the sheet production process allows for, again, an elegant and simple method, but also one that reduces or even eliminates the need for other chemicals to impart the desired production scheme. Such a pure starting material and overall production method further underscores the highly unexpected benefits of not only the method employed for such an inventive product, but the simple combination of microfibers with nanofibers and an aqueous solute for such a purpose and yet to achieve a heretofore unattainable battery separator material on demand and with the versatility for multiple end uses.

Thus, it is of great importance for the inventive method and products that the nanofiber constituents combine with the microfibers under a sufficiently high shear environment to accord the desired introduction of such nanofibers onto and within the resultant microfiber nonwoven substrate simultaneously during actual nonwoven fabrication itself. In other words, upon the provision of both types of fiber materials within the nonwoven production process, the manufacturer should accord a sufficient amount of mixing and high shear conditions to best ensure the proper degree of entanglement between the different fiber types to form the desired single-layer fabric structure. As well, the fabrication method is potentially preferred as a wet-laid nonwoven procedure in addition to the high shear type, ostensibly to best ensure the proper introduction and residual location of nanofibers within the microfiber interstices. With an increased water flow during manufacture, the extremely small nanofibers will be drawn into such interstices at a greater rate than with a dry entanglement method, thereby according the aforementioned interstice fill capability. Again, the higher the water level for such a purpose, the greater purity (and recovery of water and excess fibers, for that matter, for further utilization in a separate battery separator manufacturing process) and reliability for suitable nanofiber entanglement within the microfiber base. The resultant nonwoven structure would thus exhibit greater uniformity in terms of thickness, porosity, and, most importantly, pore sizes, therein, as well as more reliable stability for calendering to optimize thickness and pore size results, as noted above.

One method followed for such a wet-aid procedure includes the provision of pre-fibrillated microfibers in a pulp-like formulation, comprising, for example, from 50:1 to 10000:1 parts water per part of fiber (again, water alone is preferred, although, if desired, other solvents that permit a wet-laid process and subsequent facilitation of evaporation thereof may be utilized, including, for instance, certain non-polar alcohols). The pre-fibrillated microfibers have been treated in such a manner, thus exhibiting a certain amount of already-present nanofibers (the residual product removed from the microfiber themselves during fibrillation, but not removed from the overall resultant mesh of microfibers thereafter). Such pre-fibrillated microfibers and nanofibers are in pulp form as a result of the fibrillation procedure, rendering a slurry-like formulation including the above-noted aqueous-based solvent with the resultant pre-fibrillated microfibers and nanofibers. This slurry-like formulation is then mixed with selected amounts of other microfibers and/or nanofibers (preferably in pulp- or slurry-like form, as well), or the initial slurry is mixed alone, and the resultant formulation can be heated in hot water to a temperature of at least 60° C., more preferably at least 70, and most preferably at least 80, having a very low concentration of actual fiber solids content therein (i.e., below 1% and as low as less than 0.5% or even less than 0.1% by weight of water or other aqueous-based solvent). This heated dispersion is then subjected to a high shear environment with subsequent placement on a flat surface. Such a surface is sufficiently porous to allow for solvent elution, thus leaving the desired wet-laid nonwoven single fabric layer including fibrillated microfibers entangled with one another, and exhibiting interstices between each microfiber, as well as nanofibers present within such interstices and on the surface of the larger microfibers as well. The amount of added nanofibers to the pre-fibrillated microfiber pulp would thus accord greater amounts of fill between the microfiber interstices to provide an overall low mean pore size, particularly in comparison to a wetlaid nonwoven that is made solely from the pre-fibrillated pulp alone. Conversely, then, the addition of microfibers to the pre-fibrillated fiber slurry would accord a larger mean pore size to the resultant wetlaid nonwoven single layer fabric than the pre-fibrillated fiber slurry alone. This capability to target different mean pore sizes through nanofiber and/or microfiber addition levels accords the manufacturer the potential to achieve any desired mean pore size level.

Subsequent to such a high-shear mixing step, the resultant dispersion may be fed into the head of a paper machine (of any type that is capable of making light weight sheets without breaking, such as, as merely examples, Fourdrenier, Incline Wire, Rotoformer, and the like, devices). Such light weight sheets may be produced through controlling the fiber dispersion input in the head end with simultaneously controlled line speed. A set-up wherein no open draws are present (i.e., wherein the wet fiber web is unsupported) is preferred for such a method. In this situation, the high water level may be alleviated through vacuum means (which is a common step in the paper making industry), at least initially (i.e., to remove surface moisture to a certain level). For the proper thin sheet result, a fine gauge paper making wire is necessary, particularly at a gauge of at most 40 gauge, more preferably at most 80 gauge. The paper (dispersion sheet) width may be accorded any measurement as long as the production speed does not affect the end result and the overall tensile strength (particularly in an isotropic fashion) is not compromised. For efficiency purposes, the line speed may be set within a range of 25 to 1,500 ft/min, more preferably with a minimum of 50, and most preferably 1,00.

After such a paper (sheet) making step is accomplished, the formed sheet may be introduced within a drying device. Any type of standard drying means may be utilized, including heated steam cans or a hot air oven. Such heating should exceed the temperature necessary to evaporate the water (or other solvents), but should not be so high as to melt or deform the sheet itself. Such drying temperatures thus may depend upon the materials in use, as well as the sheet thicknesses, as certain materials may withstand higher temperatures than others in terms of dimensional stability and the thicker the sheet, typically the greater temperature resistance to warping or other effect.

The manufacturer may thus control the desired properties of the inventive battery separators through the capability of providing different thicknesses of the single-layer structure on demand as well. Such a thickness characteristic may be provided through the initial wet-laid fabrication method process parameters alone, or the manufacturer may subsequently calendar the resultant fabric to any desired thickness. The potential to calendar and otherwise alter the thickness of the resultant single layer fabric permits the manufacturer the further capability to allow for greater versatility in terms of both air resistance and mean pore size measurements. Such a dial-in process has yet to be explored within the battery separator industry. A calendering step utilizing typical devices, such as hard steel rolls, or a combination of a single hard steel roll and a second hard rubber roll, as merely examples, may be employed. The calendaring step may preferentially be heated to a temperature above 200° F., preferentially above 250° F., or even above 300° F. Multiple calendering steps may be undertaken as well for such a purpose, if the materials can withstand such activities without any appreciable loss of tensile strength, etc., as noted above, as well.

Resultant thicknesses of the inventive single-layer separator may thus be less than 250 micrometers, preferably less than 100 micrometers, more preferably less than 50 micrometers, even more preferably less than 35 micrometers, most preferably less than 25 micrometers. The real density of the sheets are also of importance, and these methods allow the achievement of light sheets which are useful for battery separators especially to create small, light weight batteries. As such, sheet weights below 30 grams/m² are desirable, with possible measurements below 20 grams/m², and below even 15 grams/m² potentially preferred as well As noted above, the capability of preventing contact between the anode and cathode of the battery is necessary to prevent a shorted circuit during battery use; the thickness of the separator and the controlled pore size therein provide the essential manner of achieving such a result. However, battery separator thickness may also contribute to the available volume of other component parts within the closed battery cell as well as the amount of electrolyte solution provided therein. The entirety of the circumstances involved thus require an effective separator in terms of multiple variables. The beneficial ease of manufacture as well as the capability of providing effective on-demand pore size and air resistance properties through the inventive manufacturing method and the resultant single-layer battery separator made therefrom thus sets this development distinctly apart from the state of the art battery separators currently used and marketed today.

Other methods of nonwoven sheet manufacture which enable the entanglement of a combination of nanofibers and microfibers may also be used to create the inventive battery separators. One method would be to start with distinct nanofibers and microfibers and combine them in the method described above. Other such methods include carding, cross lapping, hydroentangling, air laid, needlepunch, melt blown, spunbond or other methods or combinations of methods that enable the microfibers to form an entangled mesh and the nanofibers to fill the interstices between said microfibers.

In effect, as noted above, the microfiber interstices form the “pores” per se, and the nanofibers fill in such openings to reduce the sizes therein, and to a substantially uniform degree over the entire nonwoven structure. Of highly unexpected benefit to the overall invention, particularly in terms of targeting different levels of porosity on demand, is the ability to dial in pore sizes within the resultant nonwoven structure through the mere modification of the concentration of microfibers to nanofibers alone. Thus, for example, a 30% microfiber to 70% nanofiber proportion at the nonwoven fabrication process outset would provide a pore size in the range of 700 nm to 195 nm, whereas a 10% microfiber/90% nanofiber combination would provide an effectively smaller pore size distribution (as well as a more uniform range thereof, for example 230 nm to 130 nm). Such an unforeseen result thus accords an on-demand porosity result for the end user through, as noted, as rather simple manufacturing modification. Such pore sizes created can be measured, resulting in a mean flow pore size. Such mean flow pore sizes may be less than 2000 nm, even less than 1000 nm, preferably less than 700 nm, more preferably less than 500 nm.

Additionally, it should be noted that although a single-layer separator including microfibers and nanofibers together is encompassed within this invention, the utilization of multiple layers of such a fabric structure, or of a single layer of such an inventive battery separator fabric with at least one other layer of a different type of fabric, may be employed and still within the scope of the overall invention described herein.

Such battery separators as described herein are clearly useful for improving the art of primary and rechargeable batteries, but also may be used for other forms of electrolyte conducting energy storage techniques, such as capacitors, supercapacitors and ultracapacitors. Indeed, the control allowed on the pore size for such inventive separators may allow significant improvements in the energy loss, power discharge rate, and other properties of these devices.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is an SEM microphotograph of a prior art expanded film battery separator.

FIG. 2 is an SEM microphotograph of a prior art nanofiber nonwoven fabric battery separator.

FIGS. 3 and 4 are SEM microphotographs of one potentially preferred embodiment of an inventive microfiber/nanofiber nonwoven fabric battery separator structure.

FIGS. 5, 6, and 7 are SEM microphotographs of another potentially preferred embodiment of an inventive microfiber/nanofiber nonwoven fabric battery separator structure.

FIG. 8 shows an exploded view of an inventive rechargeable lithium ion battery including an inventive battery separator.

DETAILED DESCRIPTION OF THE DRAWINGS AND PREFERRED EMBODIMENTS

All the features of this invention and its preferred embodiments will be described in full detail in connection with the following illustrative, but not limiting, drawings and examples.

Microfiber and Nanofiber Production

As noted above, the microfiber may be constructed from any polymer (or polymer blend) that accords suitable chemical and heat resistance in conjunction with internal battery cell conditions, as well as the capability to form suitable fiber structures within the ranges indicated. Such fibers may further have the potential to be treated through a fibrillation or like technique to increase the surface area of the fibers themselves for entanglement facilitation during nonwoven fabrication. Such fibers may be made from longstanding fiber manufacturing methods such as melt spinning, wet spinning, solution spinning, melt blowing and others. In addition, such fibers may begin as bicomponent fibers and have their size and/or shape reduced or changed through further processing, such as splittable pie fibers, islands-in-the-sea fibers and others. Such fibers may be cut to an appropriate length for further processing, such lengths may be less than 50 mm, or less than 25 mm, or less than 12 mm even. Such fibers may be also be made long to impart superior processing or higher strength to have a length that is longer than 0.5 mm, longer than 1 mm, or even longer than 2 mm. Such fibers may also be fibrillated into smaller fibers or fibers that advantageously form wet-laid nonwoven fabrics.

Nanofibers for use in the current invention may be made through several longstanding techniques, such as islands-in-the-sea, centrifugal spinning, electrospinning, film or fiber fibrillation, and the like. Teijin and Hills both market potentially preferred islands-in-the-sea nanofibers (Teijin's is marketed as NanoFront fiber polyethylene terephthalate fibers with a diameter of 500-700 nm). Dienes and FiberRio are both marketing equipment which would provide nanofibers using the centrifugal spinning technique. Xanofi is marketing fibers and equipment to make them using a high shear liquid dispersion technique. Poly-aramids are produced by duPont in nanofiber state that exhibit excellent high temperature resistance, as well as other particularly preferred properties.

Electrospinning nanofiber production is practiced by duPont, E-Spin Technologies, or on equipment marketed for this purpose by Elmarco. Nanofibers fibrillated from films are disclosed in U.S. Pat. Nos. 6,110,588, 6,432,347 and 6,432,532, which are incorporated herein in their entirety by reference. Nanofibers fibrillated from other fibers may be done so under high shear, abrasive treatment. Nanofibers made from fibrillated cellulose and acrylic fibers are marketed by Engineered Fiber Technologies under the brand name EFTEC™. Any such nanofibers may also be further processed through cutting and high shear slurry processing to separate the fibers an enable them for wet laid nonwoven processing. Such high shear processing may or may not occur in the presence of the required microfibers.

Nanofibers that are made from fibrillation in general have a transverse aspect ratio that is different from those made initially as nanofibers in typical fashion (islands-in-the-sea, for instance). One such transverse aspect ratio is described in full in U.S. Pat. No. 6,110,588, which is incorporated herein by reference. As such, in one preferred embodiment, the nanofibers have a transverse aspect ratio of greater than 1.5:1, preferably greater than 3.0:1, more preferably greater than 5.0:1.

As such, acrylic, polyester, and polyolefin fibers are particularly preferred for such a purpose, with fibrillated acrylic fibers, potentially most preferred. Again, however, this is provided solely as an indication of a potentially preferred type of polymer for this purpose and is not intended to limit the scope of possible polymeric materials or polymeric blends for such a purpose.

FIGS. 1 and 2 provide photomicrographs of the typical structures of the Celgard expanded film materials and the duPont nanofiber nonwoven battery separator materials, respectively, and as discussed above. Noticeably, the film structure of the Celgard separator shows similarity in pore sizes, all apparently formed through film extrusion and resultant surface disruptions in a rather uniform format. The duPont separator is made strictly from nanofibers alone as the uniformity in fiber size and diameter is evident. Being a nonwoven structure of such nanofibers themselves, the overall tensile strengths of this separator in both machine and cross directions are very low, although roughly uniform in both directions. Thus, such a material may be handled uniformly, as a result, although overall strength lends itself to other difficulties a manufacturer must face, ultimately, if introducing such a separator into a battery cell. To the contrary, then, the FIG. 1 separator, showing the striations for pore generation in the same direction (and thus extrusion of the film in one direction), provides extremely high machine direction tensile strength; unfortunately, the tensile strength of the same material in the cross direction is very low, leaving, as discussed previously, a very difficult and highly suspect battery separator material to actually utilize in a battery manufacturing setting.

The inventive materials, shown in photomicrograph form in FIGS. 3 and 4, are of totally different structure from these two prior art products. One potentially preferred embodiment of the initial combination of microfiber and nanofibers is the EFTEC™ A-010-4 fibrillated polyacrylonitrile fibers, which have high populations of nanofibers as well as residual microfibers. The resultant nanofibers present within such a combination are a result of the fibrillation of the initial microfibers. Nonwoven sheets made of these materials are shown in FIGS. 3 and 4. By way of example, these fibers can be used as a base material, to which can be added further microfibers or further nanofibers as a way of controlling the pore size and other properties of the nonwoven fabric, or such a material may be utilized as the nonwoven fabric battery separator itself. Examples of such sheets with additional microfibers added are shown in FIGS. 5, 6 and 7. Typical properties of the acrylic Micro/Nanofibers are shown below.

TABLE 1 Acrylic Micro/Nanofiber Properties Density, g/cm³ 1.17 Tensile Strength, MPa 450 Modulus, GPa 6.0 Elongation, % 15 Typical Fiber Length, mm 4.5-6.5 Canadian Standard Freeness, ml  10-700 BET Surface Area, m²/g. 50 Moisture Regain, % <2.0 Surface Charge Anionic

Such fibers are actually present, as discussed above, in a pulp-like formulation, thereby facilitating introduction within a wetlaid nonwoven fabric production scheme.

Nonwoven Production Method

Material combinations were then measured out to provide differing concentrations of both components prior to introduction together into a wet-laid manufacturing process. Handsheets were made according to TAPPI Test Method T-205, which is incorporated here by reference (basically, as described above, mixing together in a very high aqueous solvent concentration formulation and under high shear conditions as are typically used in wet laid manufacturing and described as “refining” of fibers, ultimately laying the wet structure on a flat surface to allow for solvent evaporation). Several different combinations were produced to form final nonwoven fabric structures. The method was adjusted only to accommodate different basis weights by adjusting the initial amount of material incorporated into each sheet. Materials and ratios are shown in Table 2.

FIGS. 5, 6, and 7 correlate in structure to Example 3 below, as well. The similarity in structure (larger microfibers and smaller nanofibers) are clarified, and the presence of fewer amounts of nanofibers in these structures is evident from these photomicrographs, as well.

The fabric was measured for thickness and then cut into suitable sizes and shapes for introduction within lithium ion rechargeable battery cells. Prior to any such introduction, however, samples of the battery separator fabrics were analyzed and tested for various properties in relation to their capability as suitable battery separators. Furthermore, comparative examples of battery separator nanofiber membranes according to U.S. Pat. No. 7,112,389, which is hereby incorporated by reference, as well as battery separator films from Celgard, are reported from the tests in the patent and from Celgard product literature.

EXAMPLES

Examples 36-51 were made according to TAPPI Test Method T-205 using Engineered Fiber Technologies EFTEC™ A-010-04 fibrillated acrylic fiber (combination of microfiber and nanofiber)(listed as Base Fiber) and FiberVisions T426 fiber, which is 2 denier per filament, cut to 5 mm length, a bicomponent fiber made from polypropylene and polyethylene, and has a diameter of approximately 17 microns (listed as Added Fiber). The sheets were calendered between two hard steel rolls at 2200 pounds/linear inch at room temperature (˜25 C). The amount of each fiber, conditioned basis weight, caliper (or thickness), apparent density and porosity of the examples are shown in Table 4. Conditioned Basis Weight, Caliper, Apparent Density, and Tensile were tested according to TAPPI T220, which is hereby incorporated by reference.

TABLE 2 Separator Properties % % Conditioned Apparent Base Added Basis Wt Caliper Density Porosity Example Fiber Fiber g/m² mm g/cm³ % 36 100 0 39.9 0.065 0.614 56.2% 37 90 10 40.2 0.067 0.600 55.6% 38 80 20 39.8 0.068 0.585 55.0% 39 70 30 39.9 0.07 0.570 54.4% 40 100 0 29.98 0.051 0.588 58.0% 41 90 10 29.89 0.053 0.564 58.2% 42 80 20 28.91 0.054 0.535 58.8% 43 70 30 30.9 0.074 0.418 66.6% 44 100 0 23.58 0.044 0.536 61.7% 45 90 10 24.8 0.046 0.539 60.1% 46 80 20 24.75 0.047 0.527 59.5% 47 70 30 24.15 0.053 0.456 63.5% 48 100 0 14.8 0.03 0.493 64.8% 49 90 10 16.6 0.036 0.461 65.8% 50 80 20 16.4 0.033 0.497 61.8% 51 70 30 16.5 0.037 0.446 64.3%

The higher the porosity, the higher the peak power output within the subject battery. With such high results, theoretically, at least, the number of batteries necessary to accord the necessary power levels to run certain devices (such as hybrid automobiles, for instance) would be reduced through an increase in the available power from individual batteries. Such a benefit would be compounded with an effective air resistance barrier as well. The porosity of the inventive separator may also be controlled by the ratio of nanofiber to microfibers, the types of nanofibers, and also by post processing such as calendaring, as can be seen below.

Battery Separator Base Analysis and Testing

The test protocols were as follows:

Porosity was calculated according to the method in U.S. Pat. No. 7,112,389, which is hereby incorporated by reference. Results are reported in %, which related to the portion of the bulk of the separator that is filled with air or non-solid materials, such as electrolyte when in a battery.

Gurley Air Resistance was tested according to TAPPI Test Method T460, which is hereby incorporated by reference. The instrument used for this test is a Gurley Densometer Model 4110. To run the test, a sample is inserted and fixed within the densometer. The cylinder gradient is raised to the 100 cc (100 ml) line and then allowed to drop under its own weight. The time (in seconds) it takes for 100 cc of air to pass through the sample is recorded. Results are reported in seconds/100 cc, which is the time required for 100 cubic centimeters of air to pass through the separator.

Mean Flow Pore Size was tested according to ASTM E-1294 “Standard Test Method for Pore Size Characteristics of Membrane Filters Using Automated Liquid Porosimeter” which uses an automated bubble point method from ASTM F 316 using a capillary flow porosimeter. Tests were performed by Porous Materials, Inc., Ithaca, N.Y.

The air permeability of a separator is a measurement of the time required for a fixed volume of air to flow through a standard area under light pressure. The procedure is described in ASTM D-726-58.

TABLE 3 Tensile properties and Mean Flow Pore Size Mean Flow MD Tensile CD Tensile Pore Size Example kg/cm² kg/cm² microns 36 94 94 0.13 37 85 85 0.13 38 67 67 0.15 39 59 59 0.20 40 88 88 0.15 41 69 69 0.18 42 51 51 0.25 43 29 29 0.62 44 74 74 0.19 45 65 65 0.23 46 56 56 0.27 47 40 40 0.69 48 52 52 49 57 57 50 42 42 51 34 34

The inventive example thus shows a very small pore size mean, indicating a capability to permit a large number of recharge cycles for the subject battery. In addition, the ability to control the pore size is indicated by the change in pore size with the proportional change in the ratio of nanofiber and microfiber materials. This is a key advantage that is not present in any previous art, such that with this technology the pore size can be dialed in by the battery manufacturer depending on the requirements of the end user. Thus, a separator can be designed for a power tool or automotive application to have different characteristics from a rechargeable watch battery, cell phone or laptop computer.

The tensile properties in the examples given are isotropic, that is, the same in all directions, with no distinction between machine and cross directions. Comparative examples show tensile properties that vary considerably between machine direction (MD) and cross direction (CD) tensile strength. In general, nanofiber-based battery separators are quite weak. Thus, one advantage of the current invention is the tensile strength, which allows faster processing in battery manufacture, tighter winding of the batteries, and more durability in battery use. Such MD tensile strength is preferably greater than 25 kg/cm², more preferably greater than 50 kg/cm², and most preferably greater than 100 kg/cm². The requirements on the CD tensile strength are lower, preferably being greater than 10 kg/cm², more preferably being greater than 25 kg/cm², and most preferably greater than 50 kg/cm².

As noted above, calendering and an increased population of nanofibers relative to microfibers will reduce the overall pore size mean, even further, thus indicating, again, the ability to target certain measurements on demand for the inventive technology. Sheet production of the initial separator was then undertaken on a paper making machine (to show manufacturing may be simplified in such a manner) with such a calendering, etc., step undertaken as well.

Paper Machine Production

Two materials were then made on a rotoformer paper machine. The first, Example 52, was made from 75% EFTec A-010-4 and 25% 0.5 denier/filament polyethylene terephthalate (PET) fiber with cut length 6 mm. The second, Example 53, was made from 37.5% EFTec A-010-4, 37.5% EFTec L-010-4 and 25% PET fiber with cut length 6 mm. The fiber materials were dispersed using high shear mixing and mixed at high dilution in water, then fed into the rotoformer head box and made to sheets of weight 20 grams/m² and dried in a hot air oven. The resultant rolls were calendered at 325° F. at 2200 pounds/linear inch, resulting in thicknesses of ˜40 microns for the first sheet and 30 microns for the second sheet. Shrinkage was measured at 90° C., 130° C., and 160° C. by measuring a 12″ length in each of machine and cross direction, placing in an oven stabilized at the measuring temperature for 1 hour, and measuring the length again. The shrinkage is the change in length expressed as a percentage of the original length. Properties of the sheets are shown below in Table 4.

TABLE 4 Membrane Properties Unit of Exam- Exam- Basic Membrane Property Measure ple 52 ple 53 Thickness μm 40 30 Gurley (JIS) seconds 20 110 Porosity % 60% 55% Mean Flow Pore Size μm 0.5 0.5 TD Shrinkage @ 90 C./1 Hour % 0 0 MD Shrinkage @ 90 C./1 Hour % 0 0 TD Shrinkage @ 130 C./1 Hour % 0 0 MD Shrinkage @ 130 C./1 Hour % 2 1 TD Shrinkage @ 160 C./1 Hour % 1 0 MD Shrinkage @ 160 C./1 Hour % 4 2 TD Shrinkage @ 190 C./1 Hour % 5 0 MD Shrinkage @ 190 C./1 Hour % 1 2 TD Strength Kg/cm² 70 100 MD Strength Kg/cm² 190 170 Elongation %  4%  4%

As can be seen, the materials with both acrylic (EFTec A-010-4) and lyocell (EFTec L-010-4) materials show very good properties at high temperature. For example, many current stretched film separators may be made from polyethylene, which melts at 135° C. and shows significant shrinkage at over 110° C., or from polypropylene, which melts at 160° C. and shows significant shrinkage over 130° C. One problem that is known in the industry, especially for large format cells that might be used in electric vehicles, is that shrinkage upon exposure to high temperature can expose the electrodes to touching each other on the edges if the separator shrinks, causing a short and potentially a catastrophic thermal runaway leading to an explosion. Separators with high temperature stability thus are safer in these environments, allowing larger format cells to be used with higher energy per cell. Preferred separator performance might be to have less than 10% shrinkage at 130° C., 160° C. or 190° C. in both directions, or preferably less than 6% shrinkage or most preferably less than 3% shrinkage. In addition, the separator might be made with a component that has high temperature stability such as a lyocell, rayon, para-aramid, meta-aramid, or other fiber, that when formed into a sheet with other materials imparts a low shrinkage result, as is shown in Example 53.

Additional examples were made and tested for different calendering conditions. The paper was constructed on a Rotoformer at the Hefty Foundation facility, and consisted of 27% EFTec A-010-04 acrylic nanofiber, 53% EFTec L-010-04 lyocell nanofiber, and 20% 0.5 denier/filament polyester fiber with 5 mm cut length. The materials were mixed for 40 minutes in a 1000 gallon hydropulper, and then fed into the machine at approximately 0.25% fiber content, and a sheet made that was 15 grams/m² in areal density. This paper was calendered under different conditions, which are listed below and shown as Examples 56-60 in the Table 5 below.

Legend for Examples 56-60:

56: Calendered using the conditions above, except the rolls were not heated.

57: Sheet was fed through the calender with a second sheet of Example 56, plying the sheets together.

58: Sheet from 56 was fed through the calender with a roll of copy paper, then peeled from the copy paper.

59: Sheet from 56 was calendered with a second pass under the same conditions.

60: The plies of 57 were peeled apart, resulting in two separate sheets.

Two things can be seen from the examples below. First, the lamination of two sheets gives more than twice the Gurley air resistance of a single sheet, while lowering the total porosity. Second, calendaring a second time had the effect of increasing the porosity and lowering the Gurley. Last, the two sheets that were fed through with another sheet had the effect of increasing the Gurley and increasing the porosity at the same time. Tensile strength was decreased in all cases with additional calendering.

TABLE 5 Calendered Sheet Results Gurley Conditioned Apparent MD CD Air Basis Wt Caliper Density Porosity Tensile Tensile Resistance Example g/m² mm g/cm³ % kg/cm² kg/cm² seconds 56 14.7 0.031 0.474 59.6% 155 69 38 57 30.0 0.060 0.500 57.4% 136 53 105 58 15.2 0.037 0.412 64.9% 102 44 48 59 15.1 0.036 0.419 64.2% 99 40 34 60 15.0 0.036 0.415 64.6% 94 43 40

Wettability Testing

A square of Example 39 was taken along with a square of Celgard 2320, and a drop of 1 M LiPF6 in EC:DMC:DEC mixture (1:1:1 by volume) electrolyte was placed on the surface. After 5 seconds, the electrolyte had been completely absorbed into Example 39, with no spectral reflectance (as from the shiny surface of a liquid drop) observable. The electrolyte drop on the Celgard 2320 remained for several minutes. This is highly desirable for a lithium ion battery separator to increase the processing rate of dispersing the electrolyte, as well as to ensure uniform dispersion of the electrolyte. Non-uniform dispersion of the electrolyte is known to promote dendrite formation on repeated charge and discharge, which become defects in the cells and can lead to short circuits.

As such, it may be desirable to have a separator upon which the spectral reflectance of a drop of electrolyte deposited on the material disappears is less than 5 minutes, or less than 2 minutes, or more preferably less than 1 minute. In addition, it may be desirable to make an energy storage device from two electrodes, a separator and an electrolyte, such that the spectral reflectance of a drop of said electrolyte deposited on the separator disappears in less than 5 minutes, or less than 2 minutes, or more preferably less than 1 minute.

Other tests were undertaken involving Differential Scanning calorimetry and Thermogravimetric Analysis for Wettability measurements as well. Example 53 was tested for thermogravimetric analysis from room temperature to 1000° C. The sample showed 1.39% mass loss, ending near 100° C., which is consistent with water loss from the cellulose nanofibers and microfibers. The material showed no further degradation until approximately 300° C., when oxidation set in and a sharp decrease of approximately 60% mass between 335 and 400° C. The Example 53 was also tested for differential scanning calorimetry from room temperature to 300° C. There was a broad exotherm centered around 100° C., consistent with a release of water, and a sharper exotherm at 266° C. which onset at 250° C., consistent with the melting point of PET.

Example 52 was tested for thermogravimetric analysis from room temperature to 1000° C. The sample showed very little mass loss below 300° C., with an onset of mass loss at 335° C., and an approximately 40% mass loss up to 400° C. The Example 52 was also tested for differential scanning calorimetry from room temperature to 300° C. There was almost no signature shown between room temperature and a sharp exotherm at 266° C., onset at 250° C., consistent with the melting point of PET. In short, the curve showed no signature other than the melting of the PET microfibers.

Aramid Samples

Additional samples were made on a Rotoformer machine, similar to Examples 52 and 53.

In Example 61, four types of fibers were combined at low dilution, approximately 60 lbs in 7000 gallons of water, under very high shear conditions. The fibers were:

EFTec A-010-04 20 lbs EFTec L-010-04 20 lbs Teijin 1094 wet pulp 10 lbs 0.3 dpf PET 5 mm 10 lbs Sheets were made at 18 grams/meter², and calendered at 2200 pounds/inch and 250 degrees F. The properties of the sheets are shown below in Table NN.

In Example 62 and 63, three types of fibers were combined similar to Example 61. The fibers were:

EFTec L-010-04 20 lbs Teijin 1094 aramid wet pulp 20 lbs 0.3 dpf PET 5 mm 10 lbs Sheets were made at 18 and 15 grams/meter², Examples 62 and 63 respectively. The properties of the sheets are shown below in Table 6.

TABLE 6 Aramid-containing Sheet Properties Unit of Exam- Exam- Exam- Basic Membrane Property Measure ple 61 ple 63 ple 63 Basis Weight Grams/meter² 18 18 15 Thickness μm 43 45 43 Gurley (JIS) seconds 76 28 19 Porosity %  51%  36%  43% TD Shrinkage @ 90 C. % 0 0 0 MD Shrinkage @ 90 C. % 0 0 0 TD Shrinkage @ 160 C. % 2 1 0 MD Shrinkage @ 160 C. % 3 1 0 TD Shrinkage @ 200 C. % 3 1 1 MD Shrinkage @ 200 C. % 4 1 1 TD Shrinkage @ 240 C. % 2 2 MD Shrinkage @ 240 C. % 3 2 TD Strength Kgf/cm² 59 39 24 MD Strength Kgf/cm² 121 70 62 Elongation % 1.6% 1.6% 1.8%

As can be seen, the use of a high temperature fiber such as an aramid pulp like Teijin 1094 aramid pulp provides very low shrinkage even at high temperatures. Since batteries can be subject to thermal degradation, and this degradation can result in thermal runaway, having a component in the battery that will retain its structural shape and integrity and possibly prevent or slow down thermal runaway could be very desirable. Thus it is desirable to have a material that would shrink less than 5% at 200 C, or even less than 3%. It also may be desirable to have a material that would shrink less than 5% at 240 C, or even less than 3%. To achieve this, it may be desirable to have a component of the separator that has no melting point, glass transition temperature or thermal degradation below about 300° Celsius. In order to make the battery separator itself have thermal stability, it may be desirable to have this thermally stable fiber component at more than 5% of the total ingredients of the separator, or even more than 10%, or even more than 20%.

Battery Formation and Actual Battery Testing Results

FIG. 8 shows the typical battery 10 structure with the outside housing 12 which includes al of the other components and being securely sealed to prevent environmental contamination into the cell as well as any leakage of electrolyte from the cell. An anode 14 is thus supplied in tandem with a cathode 16, with at least one battery separator 18 between the two. An electrolyte 20 is added to the cell prior to sealing to provide the necessary ion generation. The separator 18 thus aids in preventing contact of the anode 14 and cathode 16, as well as to allow for selected ion migration from the electrolyte 20 therethrough. The general format of a battery cell follows this structural description, albeit with differing structures sizes and configurations for each internal component, depending on the size and structure of the battery cell itself. In this situation, button battery of substantially circular solid components were produced for proper testing of separator effectiveness within such a cell.

Further Battery Products and Tests

Additional pouch cell batteries were built as follows: Standard cell phone battery electrodes have a coat weight that is approximately 2.5 mAh/cm². Electrodes were produced for test procedures exhibiting a coat weight of 4 mAh/cm² (NCA) to demonstrate that the capability limits of the separator were exceeded versus standard practices as it pertained to rate capability. One cell (hand built) of each separator type was built with Celgard 2325 (Example 54, below) and Example 53 (Example 55, below). The electrodes were coated, calendered, dried, welded with tabs, put into laminate packaging, and filled with a 1M Li salt in a standard battery solvent electrolyte, and sealed. The cells were tested for discharge capacity at C/10, C/4, C/2 and C rates with several discharges at each rate, and the results are shown in Table 7 below as a percentage of the first discharge at C/10 capacity after formation. The specific discharge capacity at C/10 for the Example 54 cell was 141 mAh/g and for Example 55 cell was 145 mAh/g.

TABLE 7 Pouch Battery Measurements Rate Example 54 Example 55 C/10 100.3% 101.3% C/4 95.5% 98.3% C/2 69.5% 88.7% C 36.4% 57.1%

As can be seen from these examples, and consistent with the testing of the batteries of Examples 32-35, the battery made using the inventive separator had higher discharge capacity at higher rates, with a small advantage at C/4, but larger and significant advantages at rates of C/2 and C.

It should be understood that various modifications within the scope of this invention can be made by one of ordinary skill in the art without departing from the spirit thereof. It is therefore wished that this invention be defined by the scope of the appended claims as broadly as the prior art will permit, and in view of the specification if need be. 

What I claim is:
 1. An insulating, nonconductive microporous polymeric battery separator comprised of a single layer of enmeshed microfibers and nanofibers, wherein said battery separator further shrinks less than 5% when exposed to a temperature of 200° C. for 1 hour.
 2. The battery separator of claim 1, wherein said microfibers are entangled with one another; wherein said separator exhibits interstices between each entangled microfiber; and wherein said interstices include nanofibers present therein.
 3. The battery separator of claim 2 exhibiting a mean flow pore size of less than 2000 nm.
 4. The battery separator of claim 2 exhibiting a mean flow pore size of less than 1000 nm.
 5. The battery separator of claim 2 in which said microfibers comprise fibrillated microfibers.
 6. The battery separator of claim 5, wherein said microfibers have an average fiber diameter greater than 1000 nm.
 7. The battery separator of claim 5, wherein said microfibers have an average fiber diameter greater than 3000 nm.
 8. The battery separator of claim 5, wherein said nanofibers have an average fiber diameter less than 1000 nm.
 9. The battery separator of claim 5, wherein said nanofibers have an average fiber diameter less than 700 nm.
 10. The battery separator of claim 2 comprising nanofibers with a transverse aspect ratio greater than 1.5:1.
 11. A battery separator comprising fibers of length less than 2.54 cm (1 inch), such fibers comprising at least 5% of thermally stable fibers that have no melting point, glass transition temperature or thermal degradation below about 300° C., such battery separator having a mean flow pore size less than 2000 nm.
 12. A battery separator of claim 11, said separator further comprised of a single layer of enmeshed microfibers and nanofibers.
 13. The battery separator of claim 12, wherein said microfibers are entangled with one another; wherein said separator exhibits interstices between each entangled microfiber;
 14. The battery separator of claim 12 in which said microfibers comprise fibrillated microfibers.
 15. The battery separator of claim 12, wherein said microfibers have an average fiber diameter greater than 1000 nm.
 16. The battery separator of claim 12, wherein said microfibers have an average fiber diameter greater than 3000 nm.
 17. The battery separator of claim 12, wherein said nanofibers have an average fiber diameter less than 1000 nm.
 18. The battery separator of claim 12, wherein said nanofibers have an average fiber diameter less than 700 nm.
 19. The battery separator of claim 12 comprising nanofibers with a transverse aspect ratio greater than 1.5:1. 